GH93 instrument tube

GH93 seamless tube/high-temperature alloy tube/instrument tube/instrument protection tube/thermocouple protection tube/high-temperature resistant stainless steel tube/stainless steel tube/GH93 protective sleeve/bright instrument tube/bright protection tube/precision instrument tube/precision sleeve

Specializing in the production of nickel based high-temperature alloy pipes. All alloy materials are available; GH3030、GH3039、GH4169、Inconel600、Inconel601、Inconel690、Incoloy800H、Incoloy825、Monel400、Hastelloy C-276、Hastelloy B2、GH901、2080 3070、1560、2035、2030、2520、310、GH140、 600, 601, 800, pure nickel tube Ni, as well as those starting with J and N, etc. We warmly welcome customers to inquire or visit for guidance.

The average composition of the granular Raney nickel catalyst prepared by GH93 is Ni53.3Al43.7Fe3.0. The bed temperature is 40 ℃ and the activation treatment time is 4 hours. After alkaline solution activation treatment, wash with deionized water at 60 ℃ until the pH of the solution after washing is 7-9. Then, the zinc aqueous solution was subjected to subsequent additive modification treatment with Zn. The concentration of the zinc aqueous solution was 4.5% by weight, the weight air velocity was 1 h-1, the bed temperature was 60 ℃, and the immersion treatment time was 2.0 hours. After subsequent immersion modification treatment, wash with deionized water at 50 ℃ until the pH of the solution after washing is 7-9. The average composition of the prepared granular adsorbent is Ni54.4Al37.7Fe5.1Zn2.8.

The main production of nickel alloy materials includes nickel alloy sheets, petrochemical pipe fittings, nickel alloy seamless pipes, nickel alloy welded pipes, nickel alloy flanges, nickel alloy forgings, nickel alloy pipe fittings, nickel alloy elbows, nickel alloy tees, nickel alloy reducers, nickel alloy diameter pipes, high-temperature alloy flanges

Figure 2 is a flowchart of the preparation process of the mechanical polishing solution according to the present invention. Figure 3 shows the surface morphology of the nickel based single crystal high-temperature alloy DD403 after mechanical polishing using the present invention. Figure 4 shows the Kikuchi line pattern of nickel based single crystal high-temperature alloy DD403 collected by electron backscatter technology after mechanical polishing according to the present invention. GH3039 High temperature protective sleeve steel pipe: The present invention is further described below through the accompanying drawings and embodiments. The embodiments are not intended to be specific to the present invention, and any equivalent substitution or modification falls within the scope of protection of the present invention. 1. In Example 1, the experimental alloy DD403 was mechanically polished according to the process sequence shown in Figure 1. [0039] (2) Cleaning: Clean the DD403 sample cut in step (1) to remove any remaining oil or other contaminants on the surface of the sample. Then rinse with clean water, dehydrate with ethanol, and blow dry; [0040] In this embodiment, when using the cleaned and cut DD403 sample, a clean brush is dipped to scrub the surface of the DD403 sample, and then rinsed with clean water. As another preferred option, the conditions for high-temperature refining in step (3) are: vacuum degree of 5Pa, refining 10-20mino as another preferred option, the conditions for temperature refining in step (5) are: vacuum degree of 2Pa, refining 10-20mino as another preferred option, and the alloying elements in step (6) are Al, Ti, NiB, and Ce. Technical effect: Compared with the prior art, the present invention has advantages under W: 1. By adding carbon in three steps, the present invention more effectively causes boiling reaction between C and 0 in the alloy liquid, accelerates the mass transfer rate of N in the alloy melt by floating up C0 bubbles, and also removes it more effectively. 0 in the alloy liquid; 2. Ben. According to the following embodiments, the GH3039 high-temperature protective sleeve steel pipe can better understand the present invention.

High temperature alloy forgings, high temperature alloy fittings, high temperature alloy elbows, high temperature alloy tees, high temperature alloy reducers, high temperature composite pipes, corrosion-resistant alloy flanges, corrosion-resistant alloy forgings, corrosion-resistant alloy fittings, corrosion-resistant alloy elbows, corrosion-resistant alloy tees, corrosion-resistant alloy reducers, corrosion-resistant composite pipes

When recycling, use wire cutting to cut 7mm off the bottom end of the lead grain section of the single crystal high-temperature alloy test rod with a deviation of 4 degrees from the [001] orientation axis. When the seed crystal is reused to prepare the single crystal high-temperature alloy again, the paste like area on the seed crystal is moved down 7mm to ensure that the paste like area generated when the seed crystal is reused to prepare the single crystal high-temperature alloy does not overlap with the paste like area generated when preparing the single crystal high-temperature alloy test rod with a deviation of 4 degrees from the [001] orientation axis. Disconnect the I-th single crystal high-temperature alloy test rod with an orientation deviation of 4 degrees from the axial direction from the boundary between the selection section 2 and the seeding section 3, and recycle the seeding section 3 as a reusable seed crystal. [0054] Use 1200 # sandpaper to polish the repeatedly used seed crystal, so that the final diameter of the seed crystal is 11.78mm, the length is 43mm, and the gap with the corundum tube in the step is 0.28mm. Compared with the prior art, the present invention improves the microstructure of the material, especially the properties of the γ 'phase and MC phase And effectively precipitate the original particle boundary (PPB); Solved the problem of harmful phases in nickel based high-temperature alloys in high temperature service, and improved the fatigue performance of alloy materials. The experimental results show that its various indicators can be superior to existing high-temperature alloys, especially existing powder metallurgy high-temperature alloys. Figure 1 shows a comparison of the content of γ 'strengthening phase between alloy 140 in the embodiment of the present invention and a second-generation typical powder metallurgy high-temperature alloy at 850 ℃; Figure 2 shows a comparison of the dissolution temperature of the γ 'phase between alloy 140 in the embodiment of the present invention and a second-generation typical powder metallurgy high-temperature alloy; Figure 3 shows the embodiment of the present invention?.