US20190085432A1 - Degradable mg alloy - Google Patents

Degradable mg alloy Download PDF

Info

Publication number
US20190085432A1
US20190085432A1 US16/085,278 US201616085278A US2019085432A1 US 20190085432 A1 US20190085432 A1 US 20190085432A1 US 201616085278 A US201616085278 A US 201616085278A US 2019085432 A1 US2019085432 A1 US 2019085432A1
Authority
US
United States
Prior art keywords
mass
degradable
content
corrosion rate
alloy
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.)
Abandoned
Application number
US16/085,278
Other languages
English (en)
Inventor
Yuya Iwamoto
Yasuhide KANATSU
Akihiko Koshi
Jinsun Liao
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.)
Kurimoto Ltd
Original Assignee
Kurimoto Ltd
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 Kurimoto Ltd filed Critical Kurimoto Ltd
Assigned to KURIMOTO, LTD. reassignment KURIMOTO, LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: IWAMOTO, YUYA, KANATSU, YASUHIDE, KOSHI, AKIHIKO, LIAO, JINSUN
Publication of US20190085432A1 publication Critical patent/US20190085432A1/en
Abandoned legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • 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
    • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon

Definitions

  • the present invention relates to a degradable Mg alloy whose corrosion rate can be arbitrarily adjusted.
  • AM type Mg alloys in which Al and Mn are added and AZ type Mg alloys in which Al, Mn, and Zn are added are known as general purpose magnesium alloys (Mg alloys).
  • Mg alloys general purpose magnesium alloys
  • Patent Document 1 describes an Mg alloy in which Mg is from 67 to 85% (atomic ratio), Si is from 5 to 20% (atomic ratio), and the balance is Ni. Patent Document 1 describes that an amorphous powder or a nanocrystal powder is produced by a mechanical alloying method (mechanical alloying) using a raw material powder having such a composition. Such an Mg alloy shows excellent corrosion resistance, and is an alloy which is resistant to degradation and corrosion.
  • Patent Document 2 describes an Mg alloy containing Al: from 0.1% to 15.0%; Li: from 0.01% to 10.0%; Ca: from 0.1% to 10.0%; Zn: from 0.1% to 6.5%; In: from 0.01% to 3.0%; Ga: from 0.0% to 2.0%; Si: from 0.1% to 1.5%; Mn: from 0.0% to 0.8%; Zr: from 0.0% to 1.0%; Fe: from 0.016% to 1.0%; Ni: from 0.016% to 5.0%; and Cu: from 0.15% to 5.0%, by mass ratio.
  • This is a degradable Mg alloy used as a member which is introduced into oil wells and natural gas wells to temporarily support the structure and is degraded when it becomes unnecessary.
  • Patent Document 3 also describes as a degradable Mg alloy an alloy containing Al: from 3.0% to 7.0%; Li: from 0.01% to 1.0%; Ca: from 0.5% to 1.0%; Y: from 0.3% to 2.3%; Si: from 0.3% to 2.0%; Ni: from 0.016% to 0.8%; Cu: from 0.05% to 1.0%; and Fe: from 0.016% to 1.0%, by mass ratio.
  • Patent Document 4 describes an Mg alloy for casting containing Cu: from 0.5% to 10%, Ca: from 0.01 to 3%, and Al: from 0 to 3%, by mass ratio.
  • Patent Document 4 describes an Mg alloy that has excellent creep resistance by containing Cu and Ca and is suitable for use under high temperature environment.
  • Patent Document 1 JP2002-249801A
  • Patent Document 2 CN104004950A
  • Patent Document 3 CN104651691A
  • Patent Document 4 WO2008/072435
  • degradable Mg alloys used for structural materials to be introduced in oil fields or natural gas fields need to have sufficient mechanical properties for withstanding underground high pressure environment. Meanwhile, since such degradable Mg alloys are introduced into unrecoverable environments, such alloys are desirably degraded without being left in the ground for a long time after the introduction.
  • the degradable Mg alloy described in Patent Document 2 contains Si which has an adverse effect on elongation or toughness as an essential element. An extremely expensive In is contained as an essential element for use in a disposable member.
  • the degradable Mg alloy described in Patent Document 3 uses Si which has an adverse effect on elongation or toughness as an essential element, and the minimum content of Si is higher than that of the degradable Mg alloy of Patent Document 2.
  • the alloy of Patent Document 1 is an Mg alloy which has enhanced corrosion resistance by generating an amorphous phase or nanocrystals by using a mechanical alloying method, not by improving the degradability by the composition, and the use of the alloy is different.
  • an object of the present invention is to provide a degradable Mg alloy having a composition having a little kinds of essential elements and having strength required for a structural member that can withstand high pressure and capable of arbitrarily controlling the corrosion rate.
  • the Mg alloy satisfying these range conditions has sufficient tensile strength properties. Furthermore, the Mg alloy has the property that the corrosion rate can be adjusted by the blending amount of Ni and Cu.
  • the alloy may contain 0.0% by mass or more and 1.0% by mass or less of Zn.
  • the content of Ni is 0.01% by mass or more and 7.0% by mass or less.
  • the content of Ni is in the range of 0.01% by mass or more and 0.3% by mass or less, a correlation is established to such an extent that the relationship between the content of Ni and the corrosion rate can be approximated to a linear function.
  • the content of Cu is 1.0% by mass or more and 10.0% by mass or less.
  • the content of Ni is in the range of 1.5% by mass or more and 7.0% by mass or less, a correlation is established to such an extent that the relationship between the content of Cu and the corrosion rate can be approximated to a linear function.
  • the degradable Mg alloy has sufficient mechanical strength while requiring a few kinds of essential elements, the corrosion rate can be adjusted according to the content of Ni and Cu, and the life of a degradable structural material using the degradable Mg alloy can be arbitrarily adjusted.
  • FIG. 1 is a graph of the corrosion rate with respect to the content of Ni in Examples.
  • FIG. 2 is a schematic diagram of the shape of a test material used in Examples.
  • FIG. 3 is a graph of the corrosion rate with respect to the content of Cu in Examples.
  • the present invention relates to a degradable Mg alloy capable of accelerating corrosion at high speed mainly in an aqueous environment in which water is interposed, a degradable structural member using the same, and a method of adjusting the corrosion rate of the degradable structural member.
  • the content of Al in the degradable Mg alloy according to the present invention is needed to be 3.9% by mass or more, and is preferably 7.0% by mass or more.
  • the degradable Mg alloy has an effect of improving the strength by addition of Al, but when the content of Al is less than 3.9% by mass, such an effect is insufficient.
  • the strength is insufficient, the durability in a high-pressure environment is insufficient, and there is a high possibility that a member is destroyed before being degraded according to the adjusted degradation rate described below.
  • the Al content is required to be 14.0% by mass or less, and is preferably 13.0% by mass or less.
  • the content of Mn in the degradable Mg alloy according to the present invention needs to be 0.1% by mass or more. Mn has an effect of removing some elements contained as impurities, and when the Mn is too small, the corrosion rate of the degradable Mg alloy greatly deviates from the value adjusted by Ni and Cu, which will be described later, and the controllability may be insufficient.
  • the content of Mn needs to be 0.6% by mass or less, and is preferably 0.5% by mass or less. This is because when the content of Mn is too large, precipitation of a large amount of an intermetallic compound of Mn and Al and an Mn simple substance will make a member brittle and the strength will be lowered.
  • the degradable Mg alloy according to the present invention may contain Zn in an amount of 1.0% by mass or less.
  • Zn has an effect of improving a strength (particularly proof stress).
  • ductility is insufficient, not only a process of forming a structural member such as extrusion processing and forging processing becomes difficult but also an effect of suppressing the corrosion rate appears, which is not preferable for a degradable structural member.
  • Zn may not be contained, or Zn may be contained within the range of inevitable impurities contained in the alloy, which will be described below.
  • the degradable Mg alloy according to the present invention needs to contain Ni, Cu, or both of Ni and Cu.
  • Ni and Cu By including predetermined amounts of Ni and Cu, it is possible to arbitrarily adjust the corrosion rate in the aqueous environment of an alloy. In other words, it is possible to degrade a degradable structural member made of the degradable Mg alloy at a timing when the member becomes unnecessary.
  • both Ni and Cu contribute to degradability, their influences are different from each other, and therefore the range of desirable content that can be adjusted to the optimum corrosion rate varies.
  • the content is required to be 0.01% by mass or more.
  • Ni has a greater effect on corrosion rate than Cu, but when the content is less than 0.01% by mass, it is still difficult to obtain sufficient effect as a degradable Mg alloy.
  • the content of Ni is preferably 7.0% by mass or less. Even when Ni is excessively contained, the corrosion rate is not extremely improved, and the physical properties are difficult to control. When too much Ni is used, the cost burden becomes too large.
  • the corrosion rate (mg/cm 2 /day) can be linearly approximated to the logarithm of the content of Ni.
  • the corrosion rate of a degradable structural member produced using the degradable Mg alloy according to the content of Ni can be set with high accuracy.
  • the “corroded state” which is a criterion of the above-described corrosion rate means a state of being decomposed from a mass of the original alloy, being dissolved or dispersed in an aqueous solvent, and being not integral with the mass.
  • the content is required to be 1.0% by mass or more. Cu has less influence on the corrosion rate than Ni, and when the content is less than 1.0% by mass, it is difficult to obtain a sufficient effect as a degradable Mg alloy.
  • the Cu content is preferably 10.0% by mass or less. Even when Cu is excessively contained, the corrosion rate is not extremely improved, and the physical properties are difficult to control.
  • the corrosion rate (mg/cm 2 /day) can be linearly approximated to the logarithm of the content of Cu.
  • the corrosion rate of a degradable structural member produced using the degradable Mg alloy according to the content of Cu can be set with high accuracy.
  • Cu has less influence than Ni, adjustment with high precision becomes easy.
  • the degradable Mg alloy according to the present invention may contain both Ni and Cu, and each content may be appropriately adjusted to set an optimum corrosion rate. Since the degree of influence depends on the content, it is preferable to use this difference in adjustment. For example, fine adjustment can be made finely with Cu having a relatively small influence by the content while securing a sufficient corrosion rate with Ni having a relatively strong influence.
  • the degradable Mg alloy according to the present invention may contain other elements than the above elements as inevitable impurities. These inevitable impurities are inevitably contained contrary to intention due to manufacturing problems or problems on raw materials. Examples thereof include an element such as Ag, Fe, Pb, Cd, Se, Y, Si, Li, In, Ca, Ti, Zr, Ga, or Mm (misch metal).
  • the contents of inevitable impurities need to be in a range not inhibiting characteristics of the degradable Mg alloy according to the present invention, and the content per element is preferably less than 0.2% by mass, and more preferably less than 0.1% by mass.
  • the contents of Si, Li, In, and Ca are preferably less than 0.1% by mass, and more preferably less than 0.05% by mass.
  • the smaller the content of any element which is an inevitable impurity the more preferable, because this reduces uncertain factors to be considered in adjusting the corrosion rate by Ni and Cu. It is particularly preferable that the content is less than the detection limit.
  • the degradable Mg alloy according to the present invention is composed of Mg except for the above-described Al, Mn, Zn, Ni, Cu, and inevitable impurities.
  • the degradable Mg alloy can be prepared by a general method using raw materials containing the above elements in such a manner that the respective contents fall within the above range in terms of % by mass and the alloy has a desired corrosion rate.
  • the above value of the mass % unit is not based on the raw material, but is based on a prepared alloy or a degradable structural member produced by casting, sintering or the like. It is noted that when a degradable structural member which is particularly required to have strength is produced, it is preferable to perform processing such as extruding or forging to reduce the crystal size of the alloy texture to increase the strength.
  • the crystal size is about from 100 to 200 ⁇ m, and when the crystal size is reduced to about 10 ⁇ m or more and 20 ⁇ m or less by the above extrusion, forging, wroughting, or the like, the strength is improved, which is preferable. Even when the crystal size is miniaturized in this manner, the corrosion rate does not change significantly and the corrosion rate can be arbitrarily adjusted depending on the contents of Ni and Cu.
  • Ni is limited to a range of 0.01% by mass or more and 0.3% by mass or less and Cu is limited to a range of 1.5% by mass or more and 7.0% by mass or less
  • an increase in the corrosion rate can be suitably approximated to a linear function with respect to an increase in the logarithms of the contents of Ni and Cu.
  • the fluctuation of the content of Al, Mn, and inevitable impurities is made as small as possible, the corrosion rate of the decomposable Mg alloy corresponding to the limited range of the content of Ni or Cu is measured for a plurality of points, the inclination and intercept of the corrosion rate with respect to the logarithm of the content of Ni or Cu is calculated, the content of Ni or Cu corresponding to the required corrosion rate is determined, and the composition of the degradable Mg alloy suitable for a degradable structural member to be produced may be determined.
  • a general method such as a least-squares method may be used.
  • the degradable structural member according to the present invention has a smaller coefficient of grain size (the above-mentioned slope) than one produced by casting when the grain size is reduced by applying pressure by a technique such as extrusion, and adjustment of the corrosion rate is easier to be performed.
  • Examples of a product to which a degradable structural member made of the degradable Mg alloy according to the present invention is applied include tools for drilling oil wells, natural gas wells, and the like. Since such a product is introduced deep under the ground, a strength that can withstand a high pressure environment is required. On the other hand, when such a product becomes unnecessary, the product can be removed by being corroded and degraded at an appropriate timing by being exposed to an aqueous solution introduced for excavation work without taking time to take out from deep underground.
  • each test specimen was immersed in a 2% KCl aqueous solution (93° C.), and the corrosion weight loss (mg) of the specimen and the area before and after the test were measured to calculate the corrosion rate per day (mg/cm 2 /day: mcd).
  • the values are shown in Table 1.
  • “as-cast” is the measurement result of the test specimen by casting and “as-extruded” is the measurement result of the test specimen by extrusion processing.
  • FIG. 1 shows a graph in which Ni contents are plotted on a common logarithm scale on the horizontal axis and the corrosion rate on the vertical axis for Examples 1 to 10. However, with respect to Examples 8 to 10, only data of casting is shown.
  • Example 11 and 12 the corrosion rates of Examples 11 and 12 in which the amount of Al was reduced were measured, and the corrosion rate was measured in the same manner as in Example 1.
  • values of the corrosion rate as a degradable Mg alloy were practical.
  • the calculated value of the corrosion rate of as-cast should be 2.0 ⁇ 10 3 mcd and 2.2 ⁇ 10 3 mcd, respectively, and the calculated corrosion rate of as-extruded should be 1.2 ⁇ 10 3 mcd and 1.3 ⁇ 10 3 mcd, respectively.
  • Examples 11 and 12 were values which were particularly largely deviated from those of the extruded materials as compared with these calculated values. Thus, it is shown that, since the corrosion rate is not approximated linearly depending on the variation of the value of Al, it is desirable to unify the Al content to some extent in order to adjust the corrosion rate value with high accuracy.
  • the tensile strength, 0.2% proof stress, elongation after extrusion were measured. The measurement method is shown below and the results are shown in Table 2. In all cases, the tensile strength exceeded 275 MPa, and sufficient tensile properties and corrosion rate were exhibited as degradable structural materials to be introduced into oil fields, and the like.
  • a sample extruded as a round bar of ⁇ 16 was processed to be a 14A test piece prescribed in JIS Z2241 (ISO6892-1).
  • the specific shape is as shown in FIG. 2 .
  • the diameter d 0 of a rod-shaped portion was 10 mm
  • the original gauge length L 0 was 50 mm
  • the length L c of a cylindrical parallel portion was 70 mm
  • a tensile test was carried out in accordance with JIS Z2241 (ISO6892-1), and the tensile strength: R m (MPa), 0.2% proof stress: R p0.2 (MPa), and elongation: A (%) were evaluated as follows.
  • the tensile strength was defined as the maximum test force Fm that was tolerated during the test until the test piece showed discontinuous yield in the test.
  • the 0.2% proof stress is a stress when the plastic elongation is equal to 0.2% of the gauge distance L e of an extensometer.
  • the elongation is a value obtained by expressing the permanent elongation of a test piece after being tested until the test piece breaks as a percentage with respect to the original gauge length L 0 . All of Examples showed favorable values.
  • a test specimen was prepared by casting so as to have the composition shown in Table 3 by the same procedure as the Ni-containing alloy test described above, and the corrosion rate was measured by the same procedure. The results are shown in Table 3. For Examples 13 to 16, the corrosion rate after forging (as-forged) at a sample temperature of 430° C. was measured. Further, in Examples 17 to 23, test specimens were prepared by extrusion processing in the same manner as in the above Examples 1 to 7, and the corrosion rate was measured by the same procedure. The results are also shown in Table 3. In this Cu-containing alloy test, the value of Cu is not a measured value after the alloy was prepared but a target value at the time of addition of a material.
  • FIG. 3 shows a graph in which Cu contents are plotted on a logarithm scale on the horizontal axis and the corrosion rate on the vertical axis for Examples 17 to 23.
  • Linear approximation by the least-squares method was performed on the logarithm of Cu content and the corrosion rate value.
  • the section was ⁇ 4.0 ⁇ 10 2
  • the slope was 3.1 ⁇ 10 3 . This showed that, when casting a degradable structural material containing about 8.0 by mass of Al and about 0.18% by mass of Mn, the corrosion rate can be adjusted by the content of Cu according to the following Formula (3).

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Extrusion Of Metal (AREA)
  • Prevention Of Electric Corrosion (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)
US16/085,278 2016-03-31 2016-03-31 Degradable mg alloy Abandoned US20190085432A1 (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2016/060740 WO2017168696A1 (ja) 2016-03-31 2016-03-31 分解性Ｍｇ合金

Publications (1)

Publication Number Publication Date
US20190085432A1 true US20190085432A1 (en) 2019-03-21

Family

ID=59962807

Family Applications (1)

Application Number Title Priority Date Filing Date
US16/085,278 Abandoned US20190085432A1 (en) 2016-03-31 2016-03-31 Degradable mg alloy

Country Status (7)

Country Link
US (1) US20190085432A1 (ja)
EP (1) EP3438303B1 (ja)
JP (1) JP6692411B2 (ja)
KR (1) KR102542754B1 (ja)
CN (1) CN108884528A (ja)
PL (1) PL3438303T3 (ja)
WO (1) WO2017168696A1 (ja)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113667871A (zh) * 2021-08-10 2021-11-19 郑州轻研合金科技有限公司 一种高延展性可溶镁锂合金及其制备方法和应用
EP4047106A4 (en) * 2019-10-18 2023-01-11 Kurimoto, Ltd. DEGRADABLE MAGNESIUM ALLOY
WO2023234972A1 (en) * 2022-06-03 2023-12-07 CNPC USA Corp. Dissolvable magnesium alloy

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109750196A (zh) * 2019-03-13 2019-05-14 山东省科学院新材料研究所 一种高强度的可溶解镁合金及其制备方法
CN110129643A (zh) * 2019-06-13 2019-08-16 苏州市美新迪斯医疗科技有限公司 一种超细晶生物可降解镁合金材料及其制备方法
CN110952013B (zh) * 2019-12-24 2020-12-29 岳阳宇航新材料有限公司 一种可降解镁合金井下工具桥塞材料及其制备方法
CN111996428A (zh) * 2020-08-28 2020-11-27 深圳市苏德技术有限公司 一种可溶镁合金及其制备方法和应用
CA3199861A1 (en) * 2020-11-30 2022-06-02 Yasunobu Matsumoto Mg alloy, method for manufacturing mg alloy, and construction material and biomaterial using mg alloy
CN115466890B (zh) * 2022-09-19 2023-12-01 重庆科技学院 一种可快速降解的高强韧含Cu镁合金材料及其制备方法

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3731041B2 (ja) 2001-02-26 2006-01-05 独立行政法人産業技術総合研究所 高耐食性マグネシウム合金および高耐食性マグネシウム材料の作製方法
JP2007284743A (ja) * 2006-04-17 2007-11-01 Tetsuichi Mogi Ｍｇ合金
WO2008072435A1 (ja) 2006-12-11 2008-06-19 Kabushiki Kaisha Toyota Jidoshokki 鋳造用マグネシウム合金およびマグネシウム合金鋳物の製造方法
DE102008020523B4 (de) * 2008-04-23 2014-05-15 Helmholtz-Zentrum Geesthacht Zentrum für Material- und Küstenforschung GmbH Duktile Magnesiumlegierung
JP5405392B2 (ja) * 2009-06-17 2014-02-05 株式会社豊田中央研究所 再生マグネシウム合金とその製造方法およびマグネシウム合金
CN103397235B (zh) * 2013-08-16 2015-08-12 重庆大学 一种镁-铝-锌-锰-铜合金及其制备方法
CN104004950B (zh) * 2014-06-05 2016-06-29 宁波高新区融创新材料科技有限公司 易溶性镁合金材料及其制造方法和应用
GB201413327D0 (en) 2014-07-28 2014-09-10 Magnesium Elektron Ltd Corrodible downhole article
CN104651691B (zh) 2015-02-06 2016-08-24 宁波高新区融创新材料科技有限公司 快速降解镁合金材料及其制造方法和应用

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4047106A4 (en) * 2019-10-18 2023-01-11 Kurimoto, Ltd. DEGRADABLE MAGNESIUM ALLOY
CN113667871A (zh) * 2021-08-10 2021-11-19 郑州轻研合金科技有限公司 一种高延展性可溶镁锂合金及其制备方法和应用
WO2023234972A1 (en) * 2022-06-03 2023-12-07 CNPC USA Corp. Dissolvable magnesium alloy

Also Published As

Publication number Publication date
JP6692411B2 (ja) 2020-05-13
EP3438303A4 (en) 2019-02-06
EP3438303A1 (en) 2019-02-06
JPWO2017168696A1 (ja) 2019-02-14
KR102542754B1 (ko) 2023-06-12
EP3438303B1 (en) 2020-02-19
WO2017168696A1 (ja) 2017-10-05
KR20180125523A (ko) 2018-11-23
CN108884528A (zh) 2018-11-23
PL3438303T3 (pl) 2020-09-21

Similar Documents

Publication Publication Date Title
US20190085432A1 (en) Degradable mg alloy
AU2015248303C9 (en) Austenitic stainless steel and method for producing the same
US10876183B2 (en) High-strength seamless stainless steel pipe and method of manufacturing high-strength seamless stainless steel pipe
EP3401415A1 (en) Austenitic heat-resistant alloy and method for manufacturing same
Kawasaki et al. Developing superplasticity and a deformation mechanism map for the Zn–Al eutectoid alloy processed by high-pressure torsion
JP4493029B2 (ja) 被削性及び熱間加工性に優れたα−β型チタン合金
EP2775005A1 (en) Hot-forged copper alloy article
EP2632628B1 (de) Ni-fe-cr-mo-legierung
EP3524705A1 (en) NiCrFe ALLOY
EP3276016B1 (en) Alpha-beta titanium alloy
JP6244979B2 (ja) 低熱膨張合金
US20220220581A1 (en) Ni-Ti-BASED ALLOY MATERIAL, METHOD FOR PRODUCING Ni-Ti-BASED ALLOY MATERIAL, AND WIRE OR TUBE INCLUDING Ni-Ti-BASED ALLOY MATERIAL
Hajizadeh et al. Study of texture, anisotropy and formability of cartridge brass sheets
KR20200003794A (ko) 고강도 저열팽창 합금선
Dasharath et al. Effect of stacking fault energy on mechanical properties and strengthening mechanisms of brasses processed by cryorolling
US12000025B2 (en) Powder composition for additive manufacturing
EP4047106A1 (en) Degradable magnesium alloy
Cheng et al. Influence of rare earth on the microstructure and age hardening response of indirect-extruded Mg-5Sn-4Zn alloy
JP2015147975A (ja) 析出硬化型ステンレス鋼及びセンサー用部品
US10648067B2 (en) Precipitation strengthened metal alloy article
JP2017179478A (ja) オーステナイト系耐熱合金部材およびその製造方法
WO2018221561A1 (ja) Ｎｉ基合金及びそれを用いた燃料噴射部品、Ｎｉ基合金の製造方法
EP4083249A1 (en) Alloy
Zuberova et al. The effect of deformation processing on tensile ductility of magnesium alloy AZ31
JP6521418B2 (ja) Ｎｉ基合金及びそれを用いた燃料噴射部品、Ｎｉ基合金の製造方法

Legal Events

Date Code Title Description
AS Assignment

Owner name: KURIMOTO, LTD., JAPAN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:IWAMOTO, YUYA;KANATSU, YASUHIDE;KOSHI, AKIHIKO;AND OTHERS;SIGNING DATES FROM 20180827 TO 20180829;REEL/FRAME:046878/0646

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION