WO2017168696A1 - 分解性Mg合金 - Google Patents
分解性Mg合金 Download PDFInfo
- Publication number
- WO2017168696A1 WO2017168696A1 PCT/JP2016/060740 JP2016060740W WO2017168696A1 WO 2017168696 A1 WO2017168696 A1 WO 2017168696A1 JP 2016060740 W JP2016060740 W JP 2016060740W WO 2017168696 A1 WO2017168696 A1 WO 2017168696A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- mass
- alloy
- corrosion rate
- decomposable
- content
- Prior art date
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
-
- 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
- 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 that can be adjusted to an arbitrary corrosion rate.
- Mg alloys As general-purpose magnesium alloys (Mg alloys), AM-based Mg alloys added with Al and Mn, and AZ-based Mg alloys added with Al, Mn, and Zn are known. Various Mg alloys having improved corrosion resistance by adding elements other than these elements or changing the production method have been proposed.
- Patent Document 1 listed below describes an Mg alloy composed of 67 to 85% (atomic rate) of Mg, 5 to 20% (atomic rate) of Si, and the rest of Ni. It is described that an amorphous powder or a nanocrystalline powder is produced by a mechanical alloying method (mechanical alloying) using raw material powders having these compositions. This Mg alloy has excellent corrosion resistance and is not easily decomposed or corroded.
- Patent Document 2 by mass ratio, Al: 0.1% to 15.0%; Li: 0.01% to 10.0%; Ca: 0.1% to 10.0%; Zn: 0.1% to 6.5%; In: 0.01% to 3.0 Ga: 0.0% to 2.0%; Si: 0.1% to 1.5%; Mn: 0.0% to 0.8%; Zr: 0.0% to 1.0%; Fe: 0.016% to 1.0%; Ni: 0.016% to 5.0%; Mg alloys containing Cu: 0.15% to 5.0% are described.
- This is a degradable Mg alloy that is introduced into oil wells and natural gas wells to temporarily support the structure, and is used for members that are decomposed when they are no longer needed. It has various elements as essential elements in order to have degradability as well as strength characteristics necessary to support the structure in a high pressure environment.
- Patent Document 3 also describes a decomposable Mg alloy by mass ratio of Al: 3.0% to 7.0%; Li: 0.01% to 1.0%; Ca: 0.5% to 1.0%; Y: 0.3% to 2.3%; An alloy containing: 0.3% to 2.0%; Ni: 0.016% to 0.8%; Cu: 0.05% to 1.0%; Fe: 0.016% to 1.0% is described.
- Patent Document 4 describes a casting Mg alloy containing Cu: 0.5% to 10%; Ca: 0.01 to 3%; Al: 0 to 3% by mass ratio. An Mg alloy having excellent creep resistance by containing Cu and Ca and suitable for use in a high temperature environment is described.
- decomposable Mg alloys used for structural materials introduced into oil fields and natural gas fields need to have sufficient mechanical characteristics to withstand the high pressure environment in the ground.
- the decomposable Mg alloy described in Patent Document 2 contains Si, which has an adverse effect on elongation and toughness, as an essential element.
- it contains extremely expensive In as an essential element for use as a disposable member.
- the decomposable Mg alloy described in Patent Document 3 has Si as an essential element that adversely affects elongation and toughness, and the minimum content of Si is higher than that of the decomposable Mg alloy of Patent Document 2. Yes.
- the alloy of Patent Document 1 is an Mg alloy that has improved corrosion resistance by generating an amorphous phase or nanocrystals by using a mechanical alloying method, rather than increasing the decomposability depending on the composition, and the use is different. .
- the alloy of Patent Document 4 does not consider decomposability and corrosion characteristics at all, and Ca, which has a strong influence on the corrosion characteristics, is also added, so it is difficult to control the corrosion rate.
- the present invention provides a decomposable Mg alloy having a composition with few essential elements, having a strength necessary for a structural member that can withstand high pressure, and capable of arbitrarily controlling the corrosion rate. For the purpose.
- This invention contains 3.9 mass% or more and 14.0 mass% or less of Al, and 0.1 mass% or more and 0.6 mass% or less of Mn, Ni, Cu, or both are contained 0.01% by mass or more and 10.0% by mass or less,
- a decomposable Mg alloy the balance of which consists of Mg and inevitable impurities.
- An Mg alloy that satisfies these range conditions has sufficient tensile strength characteristics.
- this Mg alloy has a characteristic that the corrosion rate can be adjusted by the blending amounts of Ni and Cu.
- this alloy may contain 0.0 mass% or more and 1.0 mass% or less of Zn.
- Ni When Ni is contained, it is preferably 0.01% by mass or more and 7.0% by mass or less. In particular, when the Ni content is in the range of 0.01% by mass to 0.3% by mass, a correlation that can approximate the relationship between the Ni content and the corrosion rate to a linear function is established.
- Cu When Cu is contained, it is desirably 1.0% by mass or more and 10.0% by mass or less. In particular, when the Cu content is in the range of 1.5% by mass or more and 7.0% by mass or less, a correlation that can approximate the relationship between the Cu content and the corrosion rate to a linear function is established.
- the decomposable Mg alloy according to the present invention has sufficient mechanical strength while being configured with a small number of essential elements, and can adjust the corrosion rate according to the contents of Ni and Cu.
- the lifetime of the degradable structural material using the degradable Mg alloy can be arbitrarily adjusted.
- the present invention relates to a degradable Mg alloy capable of proceeding with corrosion at high speed mainly in an aqueous environment where water intervenes, a degradable structural member using the same, and a method for adjusting the corrosion rate in the degradable structural member. is there.
- the Al content needs to be 3.9% by mass or more, and preferably 7.0% by mass or more.
- the decomposable Mg alloy has the effect of improving the strength by the addition of Al, but if it is less than 3.9% by mass, these effects become insufficient. If the strength is insufficient, the durability in a high-pressure environment becomes insufficient, and there is an increased risk that the member will be destroyed before being decomposed according to the adjusted decomposition speed described later.
- the Al content needs to be 14.0% by mass or less, and is preferably 13.0% by mass or less.
- the Mn content of the decomposable 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 if it is too small, the corrosion rate of the decomposable Mg alloy will deviate greatly from the value adjusted by Ni and Cu described later, and the control is insufficient. There is a risk. On the other hand, the Mn content needs to be 0.6% by mass or less, preferably 0.5% by mass or less. If the amount is too large, an intermetallic compound of Mn and Al and Mn simple substance are precipitated in a large amount so that they become brittle and the strength is lowered.
- the decomposable Mg alloy according to the present invention may contain 1.0% by mass or less of Zn.
- Zn has the effect of improving strength (particularly yield strength). If it exceeds 1.0% by mass, ductility becomes insufficient, and the molding process of the structural member such as extrusion and forging becomes difficult, and the effect of suppressing the corrosion rate appears. Absent. On the other hand, it does not need to contain Zn, and may be a range included as an inevitable impurity described later.
- the decomposable Mg alloy according to the present invention needs to contain Ni, Cu, or both.
- Ni or Cu By including a predetermined amount of Ni or Cu, the corrosion rate of the alloy in an aqueous environment can be arbitrarily adjusted. That is, the decomposable structural member manufactured with this decomposable Mg alloy can be decomposed at a timing when it becomes unnecessary.
- Ni and Cu both contribute to decomposability, their influence is different, so the range of desirable content that enables adjustment to the optimum corrosion rate differs.
- the content needs to be 0.01% by mass or more.
- Ni has a larger influence on the corrosion rate than Cu, but if it is less than 0.01% by mass, it is difficult to sufficiently obtain the effect necessary for a decomposable Mg alloy.
- the Ni content is preferably 7.0% by mass or less. Even if contained excessively, the corrosion rate cannot be extremely improved, and the physical properties are difficult to control. Moreover, when there is too much Ni, a burden will become large also from the point of cost.
- the amount of Ni contained in the decomposable Mg alloy according to the present invention is in the range of 0.01% by mass or more and 0.3% by mass or less, with respect to the logarithm of the Ni content. / Cm 2 / day) can be approximated linearly. That is, the corrosion rate of the degradable structural member manufactured using the decomposable Mg alloy can be adjusted according to the Ni content. By utilizing this property, the time until the degradable structural member manufactured using the decomposable Mg alloy collapses can be set with high accuracy.
- the corroded state as a reference for the above corrosion rate means that the original alloy lump is decomposed, dissolved or dispersed in an aqueous solvent, and is no longer integrated with the lump.
- the decomposable Mg alloy according to the present invention contains Cu
- the content needs to be 1.0% by mass or more.
- Cu has a smaller influence on the corrosion rate than Ni, and if it is less than 1.0% by mass, it is difficult to sufficiently obtain the necessary effect as a decomposable Mg alloy.
- the Cu content is preferably 10.0% by mass or less. Even if contained excessively, the corrosion rate cannot be extremely improved, and the physical properties are difficult to control.
- the amount of Cu contained in the decomposable Mg alloy according to the present invention is in the range of 1.5% by mass or more and 7.0% by mass or less, with respect to the logarithm of the Cu content. / Cm 2 / day) can be approximated linearly. That is, the corrosion rate of the degradable structural member manufactured using the decomposable Mg alloy can be adjusted according to the Cu content. By utilizing this property, the time until the degradable structural member manufactured using the decomposable Mg alloy collapses can be set with high accuracy. In particular, since the degree of influence is smaller than that of Ni, adjustment with high accuracy is facilitated.
- the decomposable Mg alloy according to the present invention includes both Ni and Cu, and an appropriate corrosion rate may be obtained by appropriately adjusting each of them. Since the degree of influence due to the content is different, it is preferable to use this difference in the adjustment. For example, it is possible to perform finer fine adjustment with Cu having a small influence due to 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 as the inevitable impurities.
- the inevitable impurities are unavoidably contained due to problems in production or raw materials. Examples thereof include elements such as Ag, Fe, Pb, Cd, Se, Y, Si, Li, In, Ca, Ti, Zr, Ga, and Mm (Misch metal).
- the content of the decomposable Mg alloy according to the present invention needs to be in a range that does not impair the properties, and is preferably less than 0.2% by mass and more preferably less than 0.1% by mass per element. .
- Si, Li, In, and Ca are each preferably contained in an amount of less than 0.1% by mass, and more preferably less than 0.05% by mass.
- the smaller the amount of any element that is an unavoidable impurity the more preferable it is because the uncertain factors to be considered in the adjustment of the corrosion rate by Ni and Cu are eliminated, and it is particularly preferable that the element is less than the detection limit.
- the decomposable Mg alloy according to the present invention is composed of Mg except for the above Al, Mn, Zn, Ni, Cu and inevitable impurities.
- the decomposable Mg alloy according to the present invention can be prepared by a general method using raw materials containing the above elements so as to be in the above mass% range and to have a desired corrosion rate. .
- said mass% is not% in a raw material but% in the prepared alloy and the decomposable structural member manufactured by casting, sintering, etc.
- it is preferable to increase the strength by reducing the crystal size of the alloy structure by performing processing such as extrusion or forging.
- the crystal size is about 100 to 200 ⁇ m.
- the crystal size is reduced to about 10 ⁇ m or more and about 20 ⁇ m or less by the extrusion, forging, stretching, etc., the strength is improved. preferable.
- the corrosion rate does not fluctuate significantly, and the corrosion rate can be arbitrarily adjusted depending on the contents of Ni and Cu.
- the increase in corrosion rate is caused by the contents of Ni and Cu.
- Calculate the slope and intercept of the corrosion rate with respect to the logarithm of the Ni or Cu content determine the Ni or Cu content corresponding to the desired corrosion rate, and decomposable Mg alloy suitable for the degradable structural member to be manufactured It is preferable to determine the composition.
- a general method such as a least square method may be used. Note that linear approximation is possible to some extent even if the amount is less than the above-mentioned limit range, but if the amount of Ni or Cu is too small, it is difficult to adjust the actual content with high accuracy. On the other hand, if the above limit range is exceeded, the deviation from the linear function cannot be ignored.
- the coefficient of increase in corrosion rate (the above slope) is smaller than that produced by casting. It becomes easier to adjust the corrosion rate.
- Examples of products to which the degradable structural member made of the degradable Mg alloy according to the present invention is applied include drilling tools such as oil wells and natural gas wells. Since it is introduced deep into the ground, it needs to be strong enough to withstand high pressure environments. On the other hand, when it becomes unnecessary, it can be excluded by being corroded and decomposed at an appropriate timing by being exposed to an aqueous solution introduced in excavation work without taking the trouble of taking it out deep in the ground.
- Ni-containing alloy test> An example in which the decomposable Mg alloy according to the present invention was actually adjusted and the corrosion rate was measured is shown.
- the raw materials were adjusted so as to have the composition shown in Table 1, heated to 700 ° C., and a test specimen was produced by casting.
- test specimens that were extruded under conditions of a die temperature of 400 ° C. and a billet temperature of 350 ° C. were prepared. Elements other than those described are inevitable impurities of less than 0.1% by mass and Mg.
- Examples 1 to 10 a graph in which the horizontal axis represents the Ni content on a common logarithmic scale and the vertical axis represents the corrosion rate is shown in FIG. However, for Examples 8 to 10, the data is only for casting.
- the logarithm of the Ni content and the corrosion rate were linearly approximated by the method of least squares.
- the intercept was 3.4 ⁇ 10 3 and the inclination was 1.5 ⁇ 10 3 .
- the corrosion rate can be adjusted by the Ni content according to the following formula (1).
- the intercept was 2.0 ⁇ 10 3 and the inclination was 8.1 ⁇ 10 2 .
- the corrosion rate can be adjusted by the Ni content according to the following formula (2). Indicated. These approximate straight lines are also shown in FIG. In particular, it was shown that when extrusion processing is performed, the coefficient for increasing the corrosion rate is suppressed as compared with the case of casting, so that the control of the corrosion rate becomes easier.
- Example 11 and 12 with a reduced amount of Al were prepared and the corrosion rate was measured in the same manner as in Example 1, it was a practical corrosion rate value as a decomposable Mg alloy.
- the calculated values of corrosion rate of the steel should be 2.0 ⁇ 10 3 mcd and 2.2 ⁇ 10 3 mcd, respectively, and the calculated values of the as-extruded corrosion rate should be 1.2 ⁇ 10 3 mcd and 1.3 ⁇ 10 3 mcd, respectively.
- the tensile strength, 0.2% proof stress, and elongation after extrusion were measured.
- the measurement method is shown below, and the results are shown in Table 2.
- the tensile strength exceeded 275 MPa, and as a degradable structural material to be introduced into an oil field or the like, sufficient tensile properties and corrosion rate could be exhibited.
- the diameter d 0 of the rod-shaped part is 10 mm
- the original point distance L 0 is 50 mm
- the parallel part length L c in the columnar shape is 70 mm
- the test piece was subjected to a tensile test in accordance with JIS Z2241 (ISO 6892-1), and its tensile strength: R m (MPa), 0.2% proof stress: R p0.2 (MPa), and elongation. : A (%) was evaluated as follows.
- the tensile strength was defined as the maximum test force Fm that the specimen withstood during the test until it showed discontinuous yield in the test. 0.2% proof stress, the plastic elongation, a stress when becomes equal to 0.2% relative to the extensometer gauge length L e. Further, the elongation is a value expressed as a percentage of permanent elongation of the test piece after testing to failure to the original gauge length L 0. All the examples showed good values.
- ⁇ Cu-containing alloy test> A test body was prepared by casting so that the composition shown in Table 3 was obtained by the same procedure as in the Ni-containing alloy test, and the corrosion rate was measured by the same procedure. The results are shown in Table 3. In Examples 13 to 16, the corrosion rate after forging was performed under the condition of a sample temperature of 430 ° C. (as-forged) was measured. Further, for Examples 17 to 23, test specimens were prepared by extrusion as in 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 alloy production, but a target value at the time of material addition.
- Examples 17 to 23 a graph in which the horizontal axis represents the Cu content on a logarithmic scale and the vertical axis represents the corrosion rate is shown in FIG. Further, a linear approximation by the least square method was performed for the logarithm of the Cu content and the value of the corrosion rate. In the casting “as-cast”, the intercept was ⁇ 4.0 ⁇ 10 2 and the inclination was 3.1 ⁇ 10 3 . Thus, when casting a degradable structural material having Al of around 8.0 mass% and Mn of around 0.18 mass%, it was shown that the corrosion rate can be adjusted by the Cu content according to the following formula (3). .
- Examples 17 to 23 were subjected to the same tensile test as described above. As a result, all showed good values.
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)
Abstract
Description
Ni、Cu、又はその両方を0.01質量%以上10.0質量%以下含有し、
残部がMgと不可避不純物からなる分解性Mg合金により上記の課題を解決したのである。これらの範囲条件を満たすMg合金は、十分な引張強度特性を有する。なおかつこのMg合金は、Ni及びCuの配合量によって腐食速度を調整可能という特性を有する。また、この合金は、0.0質量%以上1.0質量%以下のZnを含有していてもよい。
この発明は、主に水が介在する水系環境で高速に腐食を進行させることができる分解性Mg合金、及びこれを用いた分解性構造部材、そしてその分解性構造部材における腐食速度の調整方法である。
この発明に係る分解性Mg合金を実際に調整し、腐食速度を測定した例を示す。まず、Ni含有合金について、表1に示す組成となるように原料を調整して700℃に加熱し、鋳造により試験体を作製した。また、一部の例(実施例1~3,6,7,11,12)についてはダイス温度400℃、ビレット温度350℃の条件で押し出し加工を行った試験体を作製した。記載以外の元素はそれぞれが0.1質量%未満の不可避不純物とMgである。それぞれの試験体を、2%KCl水溶液(93℃)中に浸漬し、試験体の腐食減量(mg)及び試験前後の面積を測定して一日あたりの腐食速度(mg/cm2/day:mcd)を算出した。その値を表1に示す。表中、「as-cast」が鋳造による試験体の測定結果であり、「as-extruded」が押し出し加工による試験体の測定結果である。
腐食速度(mcd:as-extruded)=8.1×102×log10(Ni)+2.0×103・・・(2)
φ16の丸棒として押し出した試料から、JIS Z2241(ISO6892-1)で規定する14A号試験片に加工した。具体的形状は図2の通りである。平行部の原断面積S0と原標点距離L0とがL0=5.65×S0 0.5の関係にある比例試験片である。棒状部の直径d0は10mm、原標点距離L0は50mm、円柱状とした平行部長さLcは70mm、肩部の半径Rは15mmとした(L0=5.65×(5×5×π)0.5=50.07)。
上記のNi含有合金試験と同様の手順により、表3に示す組成となるように、試験体を鋳造により作製し、同様の手順により腐食速度を測定した。その結果を表3に示す。また、実施例13~16についてはサンプル温度430℃の条件で鍛造を行った後(as-forged)の腐食速度を測定した。更に、実施例17~23については、上記の実施例1~7と同様に押し出し加工により試験体を作製し、同様の手順により腐食速度を測定した。その結果も表3に示す。なお、このCu含有合金試験においては、Cuの値は合金作製後の測定値ではなく、材料添加時の目標値で示す。
腐食速度(mcd:as-extruded)=1.6×103×log10(Cu)-1.2×102・・・(4)
Claims (8)
- 3.9質量%以上14.0質量%以下のAlと、0.1質量%以上0.6質量%以下のMnとを含有し、
Ni、Cu、又はその両方を、0.01質量%以上10.0質量%以下含有し、
残部がMgと不可避不純物からなる分解性Mg合金。 - 3.9質量%以上14.0質量%以下のAlと、0.1質量%以上0.6質量%以下のMnと、0.0質量%以上1.0質量%以下のZnとを含有し、
Ni、Cu、又はその両方を、0.01質量%以上10.0質量%以下含有し、
残部がMgと不可避不純物からなる分解性Mg合金。 - Niの含有量が0.01質量%以上7.0質量%以下である請求項1又は2に記載の分解性Mg合金。
- Niの含有量が0.01質量%以上0.3質量%以下である請求項1又は2に記載の分解性Mg合金。
- Cuの含有量が1.0質量%以上10.0質量%以下である請求項1乃至4のいずれかに記載の分解性Mg合金。
- Cuの含有量が1.5質量%以上7.0質量%以下である請求項1乃至4のいずれかに記載の分解性Mg合金。
- 請求項1乃至6のいずれかに記載の分解性Mg合金からなる、分解性構造部材。
- 請求項4又は6に記載の分解性Mg合金を用いた分解性構造部材において、Ni又はCuの含有量により腐食速度を調整する、分解性構造部材の腐食速度調整方法。
Priority Applications (7)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US16/085,278 US20190085432A1 (en) | 2016-03-31 | 2016-03-31 | Degradable mg alloy |
JP2018508290A JP6692411B2 (ja) | 2016-03-31 | 2016-03-31 | 分解性Mg合金 |
EP16896913.7A EP3438303B1 (en) | 2016-03-31 | 2016-03-31 | Degradable mg alloy |
KR1020187029728A KR102542754B1 (ko) | 2016-03-31 | 2016-03-31 | 분해성 Mg 합금 |
CN201680082916.3A CN108884528A (zh) | 2016-03-31 | 2016-03-31 | 降解性Mg合金 |
PCT/JP2016/060740 WO2017168696A1 (ja) | 2016-03-31 | 2016-03-31 | 分解性Mg合金 |
PL16896913T PL3438303T3 (pl) | 2016-03-31 | 2016-03-31 | Ulegający degradacji stop Mg |
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 |
---|---|
WO2017168696A1 true WO2017168696A1 (ja) | 2017-10-05 |
Family
ID=59962807
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2016/060740 WO2017168696A1 (ja) | 2016-03-31 | 2016-03-31 | 分解性Mg合金 |
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 (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2021075552A1 (ja) | 2019-10-18 | 2021-04-22 | 株式会社栗本鐵工所 | 分解性マグネシウム合金 |
JPWO2022113323A1 (ja) * | 2020-11-30 | 2022-06-02 |
Families Citing this family (7)
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 |
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 |
US20230392235A1 (en) * | 2022-06-03 | 2023-12-07 | Cnpc Usa Corp | Dissolvable magnesium 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 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2011021274A (ja) * | 2009-06-17 | 2011-02-03 | Toyota Central R&D Labs Inc | 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 |
CN103397235A (zh) * | 2013-08-16 | 2013-11-20 | 重庆大学 | 一种镁-铝-锌-锰-铜合金及其制备方法 |
US20160024619A1 (en) * | 2014-07-28 | 2016-01-28 | Magnesium Elektron Limited | Corrodible downhole article |
Family Cites Families (6)
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 |
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 |
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 |
-
2016
- 2016-03-31 EP EP16896913.7A patent/EP3438303B1/en active Active
- 2016-03-31 KR KR1020187029728A patent/KR102542754B1/ko active IP Right Grant
- 2016-03-31 JP JP2018508290A patent/JP6692411B2/ja active Active
- 2016-03-31 WO PCT/JP2016/060740 patent/WO2017168696A1/ja active Application Filing
- 2016-03-31 CN CN201680082916.3A patent/CN108884528A/zh active Pending
- 2016-03-31 US US16/085,278 patent/US20190085432A1/en not_active Abandoned
- 2016-03-31 PL PL16896913T patent/PL3438303T3/pl unknown
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2011021274A (ja) * | 2009-06-17 | 2011-02-03 | Toyota Central R&D Labs Inc | 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 |
CN103397235A (zh) * | 2013-08-16 | 2013-11-20 | 重庆大学 | 一种镁-铝-锌-锰-铜合金及其制备方法 |
US20160024619A1 (en) * | 2014-07-28 | 2016-01-28 | Magnesium Elektron Limited | Corrodible downhole article |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2021075552A1 (ja) | 2019-10-18 | 2021-04-22 | 株式会社栗本鐵工所 | 分解性マグネシウム合金 |
CN114502758A (zh) * | 2019-10-18 | 2022-05-13 | 株式会社栗本铁工所 | 可降解性镁合金 |
CN114502758B (zh) * | 2019-10-18 | 2023-01-10 | 株式会社栗本铁工所 | 可降解性镁合金 |
JPWO2022113323A1 (ja) * | 2020-11-30 | 2022-06-02 | ||
WO2022113323A1 (ja) * | 2020-11-30 | 2022-06-02 | 三協立山株式会社 | Mg合金、Mg合金の製造方法、及び、Mg合金を用いた土木材料及び生体材料 |
JP7320054B2 (ja) | 2020-11-30 | 2023-08-02 | 三協立山株式会社 | Mg合金、Mg合金の製造方法、及び、Mg合金を用いた土木材料及び生体材料 |
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 |
US20190085432A1 (en) | 2019-03-21 |
KR20180125523A (ko) | 2018-11-23 |
CN108884528A (zh) | 2018-11-23 |
PL3438303T3 (pl) | 2020-09-21 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2017168696A1 (ja) | 分解性Mg合金 | |
JP4493029B2 (ja) | 被削性及び熱間加工性に優れたα−β型チタン合金 | |
JP4189687B2 (ja) | マグネシウム合金材 | |
WO2009151031A1 (ja) | α-β型チタン合金 | |
RU2756521C2 (ru) | Подверженное коррозии скважинное изделие | |
JP2009138218A (ja) | チタン合金部材及びチタン合金部材の製造方法 | |
Higashi et al. | Microstructural evolution during superplastic flow of a binary Mg-8.5 wt.% Li alloy | |
JP6696202B2 (ja) | α+β型チタン合金部材およびその製造方法 | |
Cheng et al. | Influence of rare earth on the microstructure and age hardening response of indirect-extruded Mg-5Sn-4Zn alloy | |
US7393595B2 (en) | Composite comprising a metal or alloy and a shape memory alloy | |
JP6648894B2 (ja) | マグネシウム基合金伸展材及びその製造方法 | |
EP2157201B1 (en) | Mg-based alloy | |
Wang et al. | Transition of dominant diffusion process during superplastic deformation in AZ61 magnesium alloys | |
US20190299296A1 (en) | Aluminum alloy powder and method of producing the same, aluminum alloy extruded material and method of producing the same | |
JP6521419B2 (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 | |
JP2010222632A (ja) | 高強度Fe−Ni−Co−Ti系合金およびその製造方法 | |
WO2018061317A1 (ja) | Ni基超耐熱合金押出材の製造方法およびNi基超耐熱合金押出材 | |
Sauvage et al. | Microstructure evolution of a multiphase superalloy processed by severe plastic deformation | |
Tsutsui et al. | Superplastic deformation behavior in commercial magnesium alloy AZ61 | |
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 | |
JP6812460B2 (ja) | 高強度低熱膨張合金 | |
Lee et al. | Effects of {10–12} twins on dynamic torsional properties of extruded AZ31 magnesium alloy | |
WO2018109947A1 (ja) | マグネシウム合金の製造方法およびマグネシウム合金 | |
JP6774787B2 (ja) | マグネシウム合金の製造方法 | |
Susanti et al. | Mechanical Properties and Microstructure of Mg-1.6 Gd Alloys Reduction 80% Hot Rolling as Implant Materials |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 2018508290 Country of ref document: JP |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 20187029728 Country of ref document: KR Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2016896913 Country of ref document: EP |
|
ENP | Entry into the national phase |
Ref document number: 2016896913 Country of ref document: EP Effective date: 20181031 |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 16896913 Country of ref document: EP Kind code of ref document: A1 |